Summary of the invention
The technical problem to be solved in the present invention is to provide the hot-work die steel of a kind of large section, high tenacity, high heat-intensity.
For solving the problems of the technologies described above, the technical scheme that large section of the present invention die casting is taked with high performance hot-work die steel is:
A large section die casting high performance hot-work die steel, its innovative point is: in the chemical composition of this high performance hot-work die steel, the mass percent of each main alloy element is:
C 0.45~0.65%, Si 0.30~1.00%,
Mn 0.30~1.00%, Cr 3.50~5.50%,
Mo 2.00~3.00%, V 0.40~0.80%,
Ni 1.00~2.00%, Nb ≥0.15%,
P ≤0.02%, S ≤0.01%
Fe surplus.
On this basis, the die casting of described large section by the mass percent of each main alloy element in high performance hot-work die steel is:
C is that 0.47%, Si is that 0.30%, Mn is that 0.4%, Cr is that 4.80%, Mo is that 2.40%, V is 0.5%, P≤0.007%, S≤0.003%, and Ni is that 1.50%, Nb is 0.18%, Fe surplus.
Another technical problem that the present invention will solve is to provide the preparation technology of high performance hot-work die steel for this large section die casting.
The preparation technology of high performance hot-work die steel for the die casting of described large section, its innovative point is, this technique has following steps:
A. smelt: by large section die casting, by chemical composition and the mass percent of high performance hot-work die steel, prepare burden, electric arc furnace smelting and refining, then carry out secondary esr;
B. High temperature diffusion thermal treatment: Heating temperature is 1180~1280 ℃, soaking time is 10~15h;
C. forge hot-work: will be cooled in 1050~1200 ℃ of temperature ranges and carry out multiway forging processing through the heat treated steel ingot of High temperature diffusion, and adopt two upsettings two to pull out forging mode, and always forge compression ratio >=6, final forging temperature >=900 ℃;
D. cooling after forging: after forging, to adopt water-cooled or mist cold, guarantee that forging is cooling fast to be greater than the speed of cooling of 0.05 ℃/s, drop to 200 ℃ of following dress Annealing furnace to temperature;
E. proeutectoid carbide refinement thermal treatment: Heating temperature is 950~1150 ℃, soaking time is 5~10h, is then quickly cooled to below 250 ℃, then send annealing furnace;
F. isothermal spheroidizing is processed: first stage isothermal annealing temperature is 830~850 ℃, and annealing time is 5~10h; Subordinate phase isothermal annealing temperature is 730~750 ℃, and annealing time is 5~10h;
G. quenching and tempering thermal treatment: be heated to 950~1100 ℃, adopt oil cooling or water smoke to be cooled to below 250 ℃; Carry out subsequently 540~630 ℃ of temper, tempering 2~3 times, each tempering insulation 2~4 hours.
On this basis, in described High temperature diffusion heat treatment step, in temperature-rise period, adopt classification to heat up.
On this basis, in described quenching and tempering heat treatment step, quenching temperature is 1030 ℃, tempering twice, and each 2h, tempering temperature is 610 ℃.
The invention has the beneficial effects as follows: this hot-work die steel is compared with general H13 hot-work die steel, has suitably improved carbon content, has increased Mo content simultaneously, and added the alloying element Ni that improves hardening capacity, increased micro alloying element Nb.
1), improve a certain amount of carbon and be conducive to improve the hardening capacity of steel and urge rigidly, improve the working strength of steel;
2), the content that improves Mo element is conducive to improve thermostability and the heat resistance of steel, improves the heat-resistant anti-fatigue performance of steel simultaneously;
3), Ni is austenite stabilizer element, can greatly improve the hardening capacity of steel and improve the toughness of steel, and the free area thickness of the mould of this steel processing is increased substantially, and realizes mold sections super large;
4), the adding of microalloy Nb element, can crystal grain thinning and improve the thermostability of steel, thus improve the applied at elevated temperature performance of steel;
5) although, manganese element is weak carbide forming element, can not form carbide reinforced effect, adding of a certain amount of manganese element can promote the decomposition of cementite and postpone separating out and growing up of carbide, is conducive to the thermostability of steel.In addition, manganese element can cause the content of the residual austenite in steel to increase with stable, can improve like this toughness and the thermal fatigue resistance of steel;
6), element silicon is the effective element that improves resistance to tempering, the content that improves element silicon in steel is mainly can be so that steel martensitic decomposition in the process of tempering slows down, element silicon can effectively hinder at austenite martensitic decomposition in the drawing process after martensitic transformation, this is mainly by suppressing growing up and expanding ε-carbide stable region of ε-carbide particle, having postponed the transformation of ε-carbide to θ-carbide.Silicon is postponed ε → θ and is changed, and can fully reduce the growth rate of cementite in drawing process in steel, and Siliciumatom is separated out mutually and forms mutually the enrichment region of Siliciumatom around at θ from θ, suppresses the alligatoring of growing up of θ phase; Element silicon effectively improves the anti-temper softening ability of steel in addition;
7), in drawing process, V can reduce martensitic decomposition rate, has postponed austenitic transformation, and V-arrangement becomes the proeutectoid carbide of MC type, small and dispersed, is difficult for agglomeration, in drawing process, strengthen age hardening effect, improved greatly thermostability and the impelling strength of steel.Therefore, the content of V in steel is controlled between 0.4~0.8%, gives full play to the alloying action of V;
8), Cr main Cr23C6 type carbide that forms in hot working die steel, play strengthening effect, improve the intensity of steel;
9), this hot-work die steel is after above-mentioned thermal treatment, its hardening capacity, thermostability, impelling strength and thermal fatigue property are better than H13 steel.
Embodiment
In order to make object of the present invention, technical scheme and advantage more cheer and bright, the present invention is described further technical scheme of the present invention with following specific embodiment, but the invention is not restricted to following specific embodiment.
embodiment 1
in the present embodiment, moiety and mass percent thereof that large section die casting adopts with high performance hot-work die steel are as follows:
C 0.65%, Si 1.00%, Mn 1.00%, Cr 5.50%,
Mo 3.00%, V 0.80%, P 0.015%, S 0.007%,
Ni 2.00%, and Nb 0.20%, Fe surplus.
Technological process and the step of with the material in this embodiment, producing hot-work die steel are as follows:
A electrosmelting: carry out melting by the alloying element proportioning in the various embodiments described above in electric arc furnace, smelting temperature is greater than 1500 ℃, is cast into φ 400mm~φ 450mm electrode bar air cooling.
B esr: be positioned over the steel ingot after pouring as consumable electrode in esr device, carry out esr, change slag voltage 56~62V, voltage 57~the 59V of electric current 3000~5000A, electricity consumption system, electric current 11000~12000A, voltage 57~59V binds, current time 35~50Min, esr forms ESR ingot.
C High temperature diffusion thermal treatment: divide stepped heating by the ESR ingot after esr, guarantee that ESR ingot internal and external temperature is even, respectively at 600 ℃, 800 ℃ and 1100 ℃ of isothermal heating, be heated to 1180-1280 ℃ and carry out High temperature diffusion thermal treatment, be incubated 10~15 hours, uniform formation, improves alloying constituent segregation and eliminates liquation carbide; In this step, in order to reduce, because temperature is too low, make High temperature diffusion thermal treatment inhomogeneous, and the too short coring that makes of time is insufficient, so preferred High temperature diffusion thermal treatment temp is 1240~1260 ℃, soaking time 15h.
D forges processing: the steel ingot temperature after above-mentioned high temperature expanding thermal treatment is adjusted in 1050-1200 ℃ of temperature range and carries out multiway forging processing; The forging mode that adopts two upsettings two to pull out, always forges compression ratio >=6, final forging temperature >=900 ℃.
Cooling after E forges: after forging, to adopt water-cooled or mist cold, guarantee that forging is cooling fast to be greater than the speed of cooling of 0.05 ℃/s, drop to 200 ℃ of following dress Annealing furnace to temperature.
F proeutectoid carbide refinement thermal treatment: Heating temperature is 950~1150 ℃, soaking time is 5~10h, then adopts the mode of oil cooling or water-cooled that ESR ingot is quickly cooled to below 250 ℃, then send annealing furnace; In order to make refinement more fully completely, in this step, Heating temperature is preferably 1100 ℃, and soaking time is 10h.
G isothermal spheroidizing is processed: first stage isothermal annealing temperature is 830~850 ℃, and annealing time is 5~10h; Subordinate phase isothermal annealing temperature is 730~750 ℃, and annealing time is 5~10h; Then cool to room temperature with the furnace; In order to reduce energy consumption, the annealing time of the first stage of this step is 6h, and the annealing time of subordinate phase is 10h.
The thermal treatment of H quenching and tempering: 950~1100 ℃ of quenching temperatures, adopt the mode of oil cooling or water-cooled to quench, at 540~630 ℃, carry out 2~3 tempering, each tempering insulation time is 2~4 hours; In order to reduce energy consumption, can guarantee quenching and tempering effect again, in this step, quenching temperature is selected 1030 ℃ simultaneously, and tempering temperature is 610 ℃, tempering twice, and each time is 2h.
Hot-work die steel of the present invention is after above-mentioned smelting and hot-work and thermal treatment, and final finished specification is 500mm*800mm*4000mm module, and performance test is carried out in sampling, and analytical results is:
A transformation temperature:
Ac1, Ac3 and Ms point test result are respectively 830 ℃, 960 ℃ and 305 ℃.
B tempering characteristics:
The rational curve that tempered-hardness after 1030 ℃ of quenchings changes with tempering temperature as shown in Figure 1.
C hardness test:
Quenching hardness: 56.2HRC; Tempered-hardness: 52HRC.
D annealed structure:
The annealed structure of hot-work die steel of the present invention as shown in Figure 2.
The experiment of D impelling strength:
According in North America die casting association criterion (NADCA#207-2006) about the requirement of impact ductility test, on blank, get lateral impact sample, specimen size is 7mm * 10mm * 55mm.
Impact toughness value: >=280J during room temperature (20 ℃).
E thermostability:
Hot-work die steel of the present invention carries out stability contrast experiment with H13 steel under 620 ℃ of conditions, and H13 steel, through making its hardness value the same with steel of the present invention after the temper of quenching, is 50HRC, and test-results as shown in Figure 3.From accompanying drawing 3, although that experiment starts front hot-work die steel of the present invention is consistent with H13 steel hardness value, at 620 ℃, from carrying out 20 hours thermostabilitys, test changes in hardness situation, hot-work die steel of the present invention is better than H13 steel.
F hot fatigue performance test:
Under room temperature (20 ℃)~700 ℃ of conditions, carry out cold cycling, after 3000 cold cycling, the thermal fatigue surface topography of large section of the present invention die casting use high performance hot-work die steel as shown in Figure 4.As seen from Figure 4, after hot-work die steel thermal fatigue test of the present invention, surface crack is very even, tiny, does not see from the teeth outwards the formation of larger main crackle.The two contrast can find out, the thermal fatigue property of hot-work die steel of the present invention is better than H13 steel.
embodiment 2
In the present embodiment, moiety and mass percent thereof that large section die casting adopts with high performance hot-work die steel are as follows:
C 0.47%, Si 0.30%, Mn 0.40%, Cr 4.80%,
Mo 2.40%, V 0.50%, P 0.007%, S 0.003%,
Ni 1.50%, and Nb 0.18%, Fe surplus.
Adopt material in this embodiment to produce the technological process of hot-work die steel and step as follows with embodiment 1, repeat no more herein.
The present embodiment hot-work die steel is after above-mentioned smelting and hot-work and thermal treatment, and final finished specification is 500mm*800mm*4000mm module, and performance test is carried out in sampling, and analytical results is:
A transformation temperature:
Ac1, Ac3 and Ms point test result are respectively 831 ℃, 957 ℃ and 307 ℃.
B tempering characteristics:
The rational curve that tempered-hardness after 1030 ℃ of quenchings changes with tempering temperature as shown in Figure 5.
C hardness test:
Quenching hardness: 56.5HRC; Tempered-hardness: 51.5HRC.
D annealed structure:
The annealed structure of hot-work die steel of the present invention as shown in Figure 6.
The experiment of D impelling strength:
According in North America die casting association criterion (NADCA#207-2006) about the requirement of impact ductility test, on blank, get lateral impact sample, specimen size is 7mm * 10mm * 55mm.
Room temperature (20 ℃) impact toughness value: >=280J.
E thermostability:
Hot-work die steel of the present invention carries out stability contrast experiment with H13 steel under 620 ℃ of conditions, and H13 steel, through making its hardness value the same with steel of the present invention after the temper of quenching, is 50HRC, and test-results as shown in Figure 7.From accompanying drawing 7, although that experiment starts front hot-work die steel of the present invention is consistent with H13 steel hardness value, at 620 ℃, from carrying out 20 hours thermostabilitys, test changes in hardness situation, hot-work die steel of the present invention is better than H13 steel.
F hot fatigue performance test:
Under room temperature (20 ℃)~700 ℃ of conditions, carry out cold cycling, after 3000 cold cycling, the thermal fatigue surface topography of high performance hot-work die steel as shown in Figure 88 for the die casting of large section of the present invention.As seen from Figure 8, after hot-work die steel thermal fatigue test of the present invention, surface crack is very even, tiny, does not see from the teeth outwards the formation of larger main crackle.The two contrast can find out, the thermal fatigue property of hot-work die steel of the present invention is better than H13 steel.
embodiment 3
In the present embodiment, moiety and mass percent thereof that large section die casting adopts with high performance hot-work die steel are as follows:
C 0.45%, Si 0.50%, Mn 0.70%, Cr 3.50%,
Mo 2.00%, V 0.60%, P 0.001%, S 0.005%,
Ni 1.00%, and Nb 0.17%, Fe surplus.
Adopt material in this embodiment to produce the technological process of hot-work die steel and step with embodiment 1, repeat no more herein.
Hot-work die steel of the present invention is after above-mentioned smelting and hot-work and thermal treatment, and final finished specification is 500mm*800mm*4000mm module, and performance test is carried out in sampling, and analytical results is:
A transformation temperature:
Ac1, Ac3 and Ms point test result are respectively 831 ℃, 962 ℃ and 306 ℃.
B tempering characteristics:
The rational curve that tempered-hardness after 1030 ℃ of quenchings changes with tempering temperature as shown in Figure 9.
C hardness test:
Quenching hardness: 56HRC; Tempered-hardness: 52HRC.
D annealed structure:
The annealed structure of hot-work die steel of the present invention as shown in Figure 10.
The experiment of D impelling strength:
According in North America die casting association criterion (NADCA#207-2006) about the requirement of impact ductility test, on blank, get lateral impact sample, specimen size is 7mm * 10mm * 55mm.
Room temperature (20 ℃) impact toughness value: >=280J.
E thermostability:
Hot-work die steel of the present invention carries out stability contrast experiment with H13 steel under 620 ℃ of conditions, and H13 steel, through making its hardness value the same with steel of the present invention after the temper of quenching, is 50HRC, and test-results as shown in Figure 11.From accompanying drawing 11, although that experiment starts front hot-work die steel of the present invention is consistent with H13 steel hardness value, at 620 ℃, from carrying out 20 hours thermostabilitys, test changes in hardness situation, hot-work die steel of the present invention is better than H13 steel.
F hot fatigue performance test:
Under room temperature (20 ℃)~700 ℃ of conditions, carry out cold cycling, after 3000 cold cycling, the thermal fatigue surface topography of large section of the present invention die casting use high performance hot-work die steel as shown in Figure 12.As seen from Figure 12, after hot-work die steel thermal fatigue test of the present invention, surface crack is very even, tiny, does not see from the teeth outwards the formation of larger main crackle.The two contrast can find out, the thermal fatigue property of hot-work die steel of the present invention is better than H13 steel.
comparative example
H13 moiety and mass percent thereof are as follows:
C is that 0.39%, Si is that 1.00%, Mn is that 0.40%, Cr is that 5.20%, Mo is that 1.40%, V is that 0.90%, P is that 0.025%, S is 0.003%, Fe surplus.
The preparation of employing ordinary method, final finished specification is 500mm*800mm*4000mm module, sampling analysis:
A transformation temperature:
Ac1, Ac3 and Ms point test result are respectively 820 ℃, 890 ℃ and 340 ℃.
B tempering characteristics:
The rational curve that tempered-hardness after 1030 ℃ of quenchings changes with tempering temperature as shown in Figure 13.
C hardness test:
Quenching hardness: 52HRC; Tempered-hardness: 48HRC.
D annealed structure:
The annealed structure of hot-work die steel of the present invention as shown in Figure 14.
The experiment of D impelling strength:
According in North America die casting association criterion (NADCA#207-2006) about the requirement of impact ductility test, on blank, get lateral impact sample, specimen size is 7mm * 10mm * 55mm.
Room temperature (20 ℃) impact toughness value: >=280J.
E thermostability:
Under 620 ℃ of conditions, H13 steel carries out stability contrast experiment, and H13 steel is 48HRC through making its hardness value after the temper of quenching, and test-results as shown in Figure 15.
F hot fatigue performance test:
Under room temperature (20 ℃)~700 ℃ of conditions, carry out cold cycling, after 3000 cold cycling, the thermal fatigue surface topography of H13 steel as shown in Figure 16.